CN101230436A - Common low-carbon low-silicon hot-rolling steel belt and method for manufacturing same - Google Patents
Common low-carbon low-silicon hot-rolling steel belt and method for manufacturing same Download PDFInfo
- Publication number
- CN101230436A CN101230436A CNA2008100141837A CN200810014183A CN101230436A CN 101230436 A CN101230436 A CN 101230436A CN A2008100141837 A CNA2008100141837 A CN A2008100141837A CN 200810014183 A CN200810014183 A CN 200810014183A CN 101230436 A CN101230436 A CN 101230436A
- Authority
- CN
- China
- Prior art keywords
- rolling
- low
- hot
- steel
- temperature
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Landscapes
- Metal Rolling (AREA)
Abstract
The invention belongs to a hot-rolled steel strip and the method thereof, in particular to a common low-carbon low-silicon hot-rolled steel strip and the method thereof, or rather a common low-carbon low-silicon hot-rolled steel strip with a yield strength smaller than 270 MPa and the method thereof. The weight percentage for the components of the steel strip is as follows: C 0.05 to 0.07 percent, Si 0.01 to 0.03 percent, Mn 0.20 to 0.40 percent, P 0.008 to 0.015 percent and S 0.05 to 0.012 percent. The invention is characterized in that Als of 0.025 to 0.070 percent is added to the weight percentage and the rest is Fe. During the rough rolling and fine rolling, the starting temperature for the rough rolling is 1,160 to 1, 230 DEG C and the finishing temperature is 840 to 860 DEG C. During the coiling, the coiling temperature is 710 to 730 DEG C. The method is simple and practical and has low manufacturing as well as raw material cost and yield strength of the hot-rolled steel strip less than 270 MPa.
Description
Technical field
The invention belongs to a kind of hot rolled strip and manufacture method thereof, particularly a kind of common low-carbon low-silicon hot-rolling steel belt and manufacture method thereof relate in particular to a kind of yield strength and are lower than 270MPa common low-carbon low-silicon hot-rolling steel belt and manufacture method thereof.
Background technology
CSP is the technical process of new generation of producing hot-rolled sheet coil, compare with conventional process flow, save investment, shorten the production cycle, improve lumber recovery, aspect such as reduce production costs has a clear superiority in.Along with the develop rapidly of continuous casting and rolling technique of sheet bar in China's Iron And Steel Industry, many cold rolling mills are that raw material is produced cold-rolling deep-punching steel plate and Coated Steel with the hot-rolled coil of continuous casting and rolling technique of sheet bar production.But the production practice of home and abroad prove that the yield strength and the tensile strength of the low-carbon (LC) hot rolling thin strip that various sheet billet continuous casting and rolling production line is produced are all higher, and elongation is good.Generally more than the high 100MPa of coiled sheet than conventional hot continuous rolling machine explained hereafter, this is to the difficulty of bringing as cold rolling feeds in the production for the yield strength of the hot-rolled sheet coil that sheet billet continuous casting and rolling production line is produced.Because the yield tensile ratio height of the coils of hot-rolled steel of CSP, cause steel band hardness height after the anneal, not too be suitable for doing the deep-draw product.
In order to solve the high problem of CSP coils of hot-rolled steel yield tensile ratio, U.S. knob Ke's (Nucor) cold rolling mill uses the CSP coil of strip to make raw material, adjust metallurgically by in steel, adding boron, cooperate rolling and process for cooling, reduce its yield tensile ratio, improve the final deep drawability of product, can produce the product of DQ level.The key problem in technology that cold-rolled steel adds boron is the reasonable interpolation and the control of boron.Because boron not only dissolves in Fe and forms sosoloid in steel, also form Fe-C-B type compound and Fe-O-B type compound simultaneously with elements such as Fe, C, N, O, these two kinds of compounds all are called the B phase, and wherein Fe-C-B type compound is a fragility phase complex chemical compound.Because the B skew is gathered on austenite grain boundary, so B also mainly is deposited on the crystal boundary mutually, the B phase amount increases and alligatoring with the raising of boron content, reticulates distribution, thereby it is crisp to cause boron.The reasonable add-on of boron, generally will be according to the content of N in the steel, make the requirement of satisfied [B]=[B] of add-on-[N] * 11/14=0 of boron, this is to solve the mutually netted sedimentary effective measures of B at present, but when N content is high in the steel, just can not calculate the add-on of boron according to following formula, because the add-on of boron has an optimum upper limit, go up and prescribe a time limit when the add-on of boron surpasses this, very easily cause the crisp problem of boron, according to the practical production experience of domestic how tame steel mill, adding behind the boron intensity, to reduce amplitude little, but the crisp problem of boron that causes is but very serious.
More domestic steel mills have carried out the experimental study of ferrite rolling.Ferrite rolling is the phase transformation controlled rolling, also claim low warm machinery control, this technology is compared with traditional ausrolling technology, in the roughing district, finish to ferritic transformation by austenite, carry out finish rolling then, adopt higher coiling temperature, to obtain coarse grained ferritic structure, thereby reduce the intensity of hot rolled strip, improve plasticity.
The approach that realizes ferrite rolling is that powerful cooling system will be arranged between roughing and the finishing stand, and intermediate blank temperature before entering finishing train drops to below the Ar3, finishes the phase transformation of γ → α, and the finish rolling process is carried out in the ferrite scope fully.Ferrite rolling has strict requirement to chemical ingredients simultaneously, be applicable to that mainly carbon is lower than 0.03% low-carbon (LC) and ultra low-carbon steel, even low-carbon (LC) and ultra low-carbon steel are rolling under the ferrite transformation temperature, rolling load is big (rolling similar to the high carbon steel austenitic area) also, the domestic equipment that domestic medium-sized and small enterprises adopt is difficult to reach the condition that ferrite rolling possesses, and has to adopt traditional ausrolling technology.
Summary of the invention
The objective of the invention is to overcome above the deficiencies in the prior art, the Chemical Composition of optimization design common low-carbon low-silicon steel, adopt traditional ausrolling technology, research during phase transformation carbide separate out the regularity of distribution, by adjusting the distribution that finishing temperature and coiling temperature and laminar flow cooling technology change carbide, reach the purpose that the steel band yield strength is lower than 270MPa, reduce production costs, satisfy cold-rolled steel.
For reaching above purpose, the technical solution adopted in the present invention is: a kind of common low-carbon low-silicon hot-rolling steel belt, the composition weight proportion of its steel band is C:0.05%-0.07%, Si:0.01%-0.03%, Mn:0.20%-0.40%, P:0.008%-0.015%, S:0.005%-0.012%, it is characterized in that having added in the composition weight proportion Als of 0.025%-0.070%, surplus is Fe.
A kind of manufacture method of common low-carbon low-silicon hot-rolling steel belt, finish by following steps: hot metal pretreatment, converter smelting, purification of molten steel and continuous casting control, roughing and finish rolling, batch, it is characterized in that:
(1) in roughing and finish rolling step, the roughing start rolling temperature is 1160-1230 ℃, and finishing temperature is 840-860 ℃;
(2) in batching step, coiling temperature is 710-730 ℃.
The present invention also implements by following technique means:
Heater for rolling steel stove hall temperature upper limit is set to 1320 ℃, installs the stay-warm case that length is 70m on the conveyor roller before and after the R1 milling train; When thickness of strips was 2.30-2.50mm, the finish rolling roll speed was 8.5m/s; When thickness of strips was 2.50-2.90mm, the finish rolling roll speed was 8.0m/s; During thickness of strips 〉=3.00mm, the finish rolling roll speed is 7.6m/s.
The draft setting range of finishing stand F7 is 8-15%.
In order to guarantee that steel have good punching performance, design considerations of the present invention is:
1, steel billet Composition Control
(1) C content controls to 0.06% ± 0.01%.By the decarburization of converter operation, can only control to 0.06%-0.08% to the finished product carbon content usually, endpoint carbon content is crossed to hang down and can be caused molten steel oxidation strong excessively, influences steel product cost, quality;
(2) Si when cold rolling rolling load and cold rolling after zinc-plated considerable influence arranged all, therefore must control to below 0.03%;
(3) reduce harmful element, control P≤0.015%, S≤0.012% as far as possible;
(4) [0]≤40 * 10 in the strict control steel
-6, [N]≤50 * 10
-6, prevent that oxygen content in steel is too high and cause that inclusion increases and the too high intensity that causes of the N that dissociates improves phenomenon, otherwise can worsen the forming property of steel band.
2, control crystal boundary state
The intensity of metal is made up of intracrystalline intensity (gravitation of intragranular atom) and grain-boundary strength (bonding force of crystal boundary) two portions, and grain-boundary strength is greater than intracrystalline intensity under the normal temperature.
Crystal boundary is to the influence of intensity, and crystal boundary has inhibition to deformation.Multicrystal yield strength σ
SWith average grain diameter d concern available Hall-Page (Hall-Petch) formulate: σ
S=σ
0+ Kd
-1/2
σ
0---the yield strength of single crystal, K---grain-boundary strengthening coefficient, d---average grain diameter;
In the material of low carbon low silicon steel hot-rolled sheet, except the crystal grain matrix is exactly a crystal boundary.The present invention mainly solves: the one, and the problem of crystal grain matrix, the 2nd, the problem of solution crystal boundary.Low carbon low silicon steel hot-rolled sheet crystal grain matrix to the contribution of material yield intensity near 50%, still, σ
H(the surrender component of desirable iron-carbon alloy single crystal) is indeclinable, σ
G(the solution strengthening component of single crystal) changes with composition, but rangeability is little.Therefore, the target of reduction low carbon low silicon steel hot-rolled sheet yield strength can not a crystal grain matrix at material.
It is very big to the influence of intensity to change grain-size, and coarsened grain is to reduce the effective means of intensity.But in actual production process, find, grain fineness number can only increase to about the 8-10 level, can change the crystal boundary state, the minimizing of precipitate on the crystal boundary by improving coiling temperature, reduce crystal boundary inhibition to dislocation when distortion, can reduce intensity to a certain extent.
Select rational finishing temperature and coiling temperature, control phase-change organization and crystal boundary state by control laminar flow cooling system.Change the crystal boundary state by improving coiling temperature, the coiling temperature height, cementite is assembled, and the cemetite lamellae interlamellar spacing increases, and sorbite, troostite size are bigger, and the quantity that distributes along crystal boundary reduces.The minimizing of precipitate on the crystal boundary reduces crystal boundary inhibition to dislocation when distortion, thereby reaches the purpose that reduces intensity.
Beneficial effect of the present invention is: produce hot-rolled low carbon low-silicon steel band reduction intensity method with present thin slab and compare, do not need to add alloy, adopt traditional austenitic area rolling, manufacturing cost and material cost are low, method is simple, the hot rolled strip intensity of being produced satisfies cold rolling user's requirement less than 270MPa.
Embodiment
According to technical scheme of the present invention, adopt the continuously cast bloom that 60 tons of top-blown oxygen converters of our company+straight arc billet continuous casting machine is produced, the wide 850mm of slab specification * thick 150mm * long 9800mm.On the 950mm hot rolls, adopt the controlled rolling technology for controlled cooling to produce, the rolling thickness specification is the steel band of 2.35mm, 2.75mm and 3.25mm respectively, every kind of specification is an embodiment, specimen coding is respectively 1,2,3, Chemical Composition sees Table 1, and temperature, speed control in the rolling technology see Table 2, and mechanical property sees Table 3.
Molten iron desulfurization handle and slagging-off after, the 60 tons of top-blown oxygen converters of packing into, sulphur content is not more than 0.010%, phosphorus content is less than 0.080%, molten iron temperature is controlled at 1260-1300 ℃, the molten iron dregginess is less than 0.08%.End point carbon is controlled at 0.03-0.05%, and oxygen level is controlled at 600 * 10 in the blow end point steel
-6Below, tapping temperature is controlled at 1650 ℃-1670 ℃.Be composite deoxidant with aluminium ferromanganese and low carbon ferromanganese in the tapping process, the ladle temperature is controlled at 1595 ℃-1610 ℃.Tap hole does not loose and flows, and the tapping time is adopted slag retaining cap and slag-blocking ball pushing off the slag operation greater than 1.5min, and thickness of slag layer is less than 15mm in the ladle.Add top slag agent 0.5-1.5 kg/ton steel after having gone out steel in ladle, the top basicity of slag is at 2.15-2.75.
Control argon flow amount 0.3-0.45m before feeding aluminum steel
3/ min, Argon adopts weak stirring the (not exposed with molten steel is principle) after the line feeding, and argon flow amount is controlled at 0.08-0.13m
3/ min, wire-feeding velocity 200m/min according to [O] content, once decides oxygen less than 5 * 10 behind hello the aluminum steel
-6, 3min thermometric sampling is immediately finished in line feeding, hangs and delivers to straight arc billet continuous casting machine, and middle bag first stove adds calcium iron powder (being not more than 20kg), and casting process does not add the calcium iron powder, and teeming temperature is controlled at 1540 ℃-1565 ℃, and pulling rate is controlled at 1.2-1.4m/min.
The Chemical Composition of table 1 embodiment steel billet, wt%
| Specimen coding | C | Si | Mn | P | S | Als |
| 1 | 0.063 | 0.018 | 0.35 | 0.013 | 0.009 | 0.043 |
| 2 | 0.058 | 0.023 | 0.27 | 0.012 | 0.011 | 0.035 |
| 3 | 0.065 | 0.025 | 0.36 | 0.008 | 0.010 | 0.039 |
Slab is produced the back hot charging and is sent into heat accumulating type walking beam heater for rolling steel, and the steel slab surface temperature is more than 700 ℃, and the buck base will guarantee slab time inside furnace 〉=120 minute to guarantee that the austenite crystal after the phase transformation is fully grown up.The burner hearth top temperature is restricted to 1320 ℃, and heating zone and soaking zone fire box temperature are controlled at 1250-1320 ℃, guarantees the higher tapping temperature of strand.
On the 950mm hot rolls, 1160-1230 ℃ of roughing start rolling temperature, roughing De-scaling box and E1 dephosphorization point are removed the slab stove and are given birth to iron scale and secondary iron scale, become intermediate blank through rolling five passages of R1, are rolled into middle volume by the Coil Box that is arranged between roughing and the finish rolling.For guaranteeing to enter the temperature of finish rolling, intermediate blank adopts bigger thickness to reduce temperature drop according to the ability of finishing mill, according to thickness of strips operated by rotary motion 24-28mm, installs the stay-warm case that length is 70m simultaneously on the conveyor roller before and after the R1 milling train.
Coil Box is batched rolling with intermediate blank, and the homogeneity of at the uniform velocity rolling assurance steel band finish rolling finishing temperature is adopted in finish rolling.Finishing temperature 840-860 ℃.Be control finish rolling finishing temperature, adopt the roll speed that is higher than rolling straight carbon steel, thickness of strips is in the 2.30-2.50mm scope time, and the finish rolling roll speed is 8.5m/s; Thickness of strips is in the 2.50-2.90mm scope time, and the finish rolling roll speed is 8.0m/s, and during thickness of strips 〉=3.00mm specification, the finish rolling roll speed is 7.6m/s.Manually water coolant between the control finishing stand is accurately controlled the steel band finishing temperature.
Increase the load of finish rolling leading portion frame, reduce the cumulative deformation in non-recrystallization district, coarsened grain.The draft setting range of finishing stand F7 is 8-15%.
Coiling temperature is 710-730 ℃, by the laminar flow cooling, adopts the back segment type of cooling; For accurately controlling coiling temperature, manual fine-tuning accurate adjustment district coiling temperature.
Temperature, speed control in the table 2 embodiment rolling technology
| Specimen coding | Thickness specification mm | Heating temperature ℃ | Finishing temperature ℃ | Finish rolling speed m/s | Coiling temperature ℃ | Speed of cooling ℃/S |
| 1 | 2.35 | 1302 | 856 | 8.5m/s | 713 | 32 |
| 2 | 2.75 | 1296 | 857 | 8.0m/s | 717 | 35 |
| 3 | 3.25 | 1287 | 851 | 7.6m/s | 722 | 33 |
Table 3 embodiment mechanical property
| Specimen coding | Thickness specification mm | Yield strength MPa | Tensile strength MPa | Elongation % |
| 1 | 2.35 | 264 | 317 | 45 |
| 2 | 2.75 | 258 | 309 | 43 |
| 3 | 3.25 | 262 | 313 | 46 |
Claims (4)
1. common low-carbon low-silicon hot-rolling steel belt, the composition weight proportion of its steel band is C:0.05%-0.07%, Si:0.01%-0.03%, Mn:0.20%-0.40%, P:0.008%-0.015%, S:0.005%-0.012% is characterized in that having added the Als of 0.025%-0.070% in the composition weight proportion, surplus is Fe.
2. method of making the described common low-carbon low-silicon hot-rolling steel belt of claim 1, finish by following steps: hot metal pretreatment, converter smelting, purification of molten steel and continuous casting control, roughing and finish rolling, batch, it is characterized in that:
(1) in roughing and finish rolling step, the roughing start rolling temperature is 1160-1230 ℃, and finishing temperature is 840-860 ℃;
(2) in batching step, coiling temperature is 710-730 ℃.
3. the manufacture method of common low-carbon low-silicon hot-rolling steel belt according to claim 2, it is characterized in that: when thickness of strips was 2.30-2.50mm, the finish rolling roll speed was 8.5m/s; When thickness of strips was 2.50-2.90mm, the finish rolling roll speed was 8.0m/s; During thickness of strips 〉=3.00mm, the finish rolling roll speed is 7.6m/s.
4. according to the manufacture method of claim 2 or 3 described common low-carbon low-silicon hot-rolling steel belts, it is characterized in that: the draft setting range of finishing stand F7 is 8-15%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNA2008100141837A CN101230436A (en) | 2008-02-26 | 2008-02-26 | Common low-carbon low-silicon hot-rolling steel belt and method for manufacturing same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNA2008100141837A CN101230436A (en) | 2008-02-26 | 2008-02-26 | Common low-carbon low-silicon hot-rolling steel belt and method for manufacturing same |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN101230436A true CN101230436A (en) | 2008-07-30 |
Family
ID=39897242
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNA2008100141837A Pending CN101230436A (en) | 2008-02-26 | 2008-02-26 | Common low-carbon low-silicon hot-rolling steel belt and method for manufacturing same |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101230436A (en) |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102836872A (en) * | 2012-09-21 | 2012-12-26 | 莱芜市泰山冷轧板有限公司 | Production method for cold-rolled steel strip used for outdoor furniture |
| CN103521518A (en) * | 2013-10-14 | 2014-01-22 | 云南昆钢新型复合材料开发有限公司 | Hot continuous rolling production method of stainless steel composite board strip coil |
| CN103952636A (en) * | 2014-05-20 | 2014-07-30 | 唐山瑞丰钢铁（集团）有限公司 | Production technique of hot-rolled strip steel for cold-rolling hot-galvanizing |
| CN104975225A (en) * | 2015-07-14 | 2015-10-14 | 山东众冠钢板有限公司 | High-strength and corrosion-resistance SPHC steel plate and preparing method thereof |
| CN105088064A (en) * | 2015-08-31 | 2015-11-25 | 武汉钢铁(集团)公司 | Cladding layer steel for 340 MPa grade automobile large beams and production method |
| CN105648321A (en) * | 2016-01-22 | 2016-06-08 | 唐山国丰钢铁有限公司 | Production process for barrel-making hot dip galvanized steel strip |
| CN106271449A (en) * | 2016-08-31 | 2017-01-04 | 云南德胜钢铁有限公司 | A kind of technique using bloom production fine grain valve snail reinforcing bar |
| CN106591708A (en) * | 2016-12-21 | 2017-04-26 | 山东钢铁股份有限公司 | Production method for producing low-carbon low-silicon and aluminum-containing steel through short process |
| CN109881102A (en) * | 2019-03-19 | 2019-06-14 | 首钢集团有限公司 | A kind of mild steel and its manufacturing method |
| CN112207138A (en) * | 2020-09-25 | 2021-01-12 | 攀钢集团西昌钢钒有限公司 | Method for stably controlling finish rolling temperature of high-grade pipeline steel |
| CN114226453A (en) * | 2021-10-29 | 2022-03-25 | 马鞍山钢铁股份有限公司 | Low-carbon steel and manufacturing method for improving performance uniformity of low-carbon steel rolled by ferrite in CSP process |
-
2008
- 2008-02-26 CN CNA2008100141837A patent/CN101230436A/en active Pending
Cited By (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102836872A (en) * | 2012-09-21 | 2012-12-26 | 莱芜市泰山冷轧板有限公司 | Production method for cold-rolled steel strip used for outdoor furniture |
| CN103521518A (en) * | 2013-10-14 | 2014-01-22 | 云南昆钢新型复合材料开发有限公司 | Hot continuous rolling production method of stainless steel composite board strip coil |
| CN103521518B (en) * | 2013-10-14 | 2015-08-05 | 云南昆钢新型复合材料开发有限公司 | The hot continuous rolling process of stainless plate strip coil |
| CN103952636A (en) * | 2014-05-20 | 2014-07-30 | 唐山瑞丰钢铁（集团）有限公司 | Production technique of hot-rolled strip steel for cold-rolling hot-galvanizing |
| CN103952636B (en) * | 2014-05-20 | 2016-08-24 | 唐山瑞丰钢铁（集团）有限公司 | Cold rolling hot dip galvanizing hot-strip production technology |
| CN104975225A (en) * | 2015-07-14 | 2015-10-14 | 山东众冠钢板有限公司 | High-strength and corrosion-resistance SPHC steel plate and preparing method thereof |
| CN105088064B (en) * | 2015-08-31 | 2017-12-08 | 武汉钢铁有限公司 | A kind of 340MPa levels automotive frame coated steel and production method |
| CN105088064A (en) * | 2015-08-31 | 2015-11-25 | 武汉钢铁(集团)公司 | Cladding layer steel for 340 MPa grade automobile large beams and production method |
| CN105648321A (en) * | 2016-01-22 | 2016-06-08 | 唐山国丰钢铁有限公司 | Production process for barrel-making hot dip galvanized steel strip |
| CN106271449A (en) * | 2016-08-31 | 2017-01-04 | 云南德胜钢铁有限公司 | A kind of technique using bloom production fine grain valve snail reinforcing bar |
| CN106591708A (en) * | 2016-12-21 | 2017-04-26 | 山东钢铁股份有限公司 | Production method for producing low-carbon low-silicon and aluminum-containing steel through short process |
| CN109881102A (en) * | 2019-03-19 | 2019-06-14 | 首钢集团有限公司 | A kind of mild steel and its manufacturing method |
| CN112207138A (en) * | 2020-09-25 | 2021-01-12 | 攀钢集团西昌钢钒有限公司 | Method for stably controlling finish rolling temperature of high-grade pipeline steel |
| CN114226453A (en) * | 2021-10-29 | 2022-03-25 | 马鞍山钢铁股份有限公司 | Low-carbon steel and manufacturing method for improving performance uniformity of low-carbon steel rolled by ferrite in CSP process |
| CN114226453B (en) * | 2021-10-29 | 2023-04-28 | 马鞍山钢铁股份有限公司 | Manufacturing method for low-carbon steel and improving performance uniformity of ferrite-rolled low-carbon steel |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101230436A (en) | Common low-carbon low-silicon hot-rolling steel belt and method for manufacturing same | |
| CN102199720B (en) | Low carbon steel sheet with yield strength over 400MPa and manufacturing method thereof | |
| CN102899556B (en) | Production method for low-alloy medium-thick steel plate | |
| CN102002628B (en) | Method for manufacturing low-carbon steel sheets | |
| CN101845599B (en) | Weathering steel and manufacturing method thereof | |
| CN101805873B (en) | Low-cost and high-strength steel for automobile crossbeam and manufacturing method thereof | |
| CN104233064B (en) | Cold rolling IF high-strength steel and the production method thereof of phosphorating of a kind of 170MPa level | |
| CN103509996B (en) | The manufacture method of tensile strength 400MPa grade high-strength carbon manganese structure iron | |
| CN104928595A (en) | Band steel with good cold forming performance and for automobile structure and production process thereof | |
| CN108842024A (en) | A kind of phosphorous IF high-strength steel band of 390MPa grades of cold rolling and its LF-RH duplex production technology | |
| CN101654760B (en) | Unalloyed structural steel S355J2 steel plate and production method thereof | |
| CN102719743A (en) | Hot-rolled coil plate for oil casing and manufacturing method thereof | |
| CN107419078A (en) | Yield strength 345MPa level low cost hot rolled steel plates and its manufacture method | |
| CN101906570A (en) | Tinning substrate for deep-punching food can and production method thereof | |
| CN112011737B (en) | 390 MPa-grade-20-DEG C-resistant hot-rolled angle steel for bridge structure and production method thereof | |
| CN107475627B (en) | 600MPa grade analysis of producing hot rolled TRIP and manufacturing method based on CSP process | |
| CN106399835A (en) | Production method of high-strength automobile hub steel | |
| CN102912224B (en) | Production method for low-alloy medium-thickness steel plate | |
| CN102925799B (en) | A kind of production method of ultra-high strength steel plate | |
| CN104561826B (en) | Low-alloy high-tensile structural steel Q460C strip steel and its production technology | |
| CN104342598A (en) | Production method of hot rolled steel strip for 600 MPa-level automotive frame | |
| CN102978511B (en) | Method for producing hot-rolled steel plate for automobile girder steel by low cost | |
| CN100560773C (en) | A kind of high-strength anti-fatigue steel products and manufacture method thereof | |
| CN110144524A (en) | A kind of 440MPa grades of cold rolling gap-free atom high-strength steel and its CSP+BAF production method | |
| CN102912223B (en) | Production method for low-alloy medium-thick steel sheet |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C02 | Deemed withdrawal of patent application after publication (patent law 2001) | ||
| WD01 | Invention patent application deemed withdrawn after publication |
Open date: 20080730 |